EP0436723B1 - Oxyde supraleitfahiges mittel und verfahren zur herstellung - Google Patents

Oxyde supraleitfahiges mittel und verfahren zur herstellung Download PDF

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EP0436723B1
EP0436723B1 EP90910173A EP90910173A EP0436723B1 EP 0436723 B1 EP0436723 B1 EP 0436723B1 EP 90910173 A EP90910173 A EP 90910173A EP 90910173 A EP90910173 A EP 90910173A EP 0436723 B1 EP0436723 B1 EP 0436723B1
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ba2cu4o8
phase
oxide superconductor
powder
oxide
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EP0436723A4 (en
EP0436723A1 (de
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T. Superconductivity Research Laboratory Miyatake
N. Superconductivity Research Lab. Koshizuka
Seiji Hayashi
Kazuyuki Shibutani
Yoshio Kawate
Yoshio Masuda
Rikuo Ogawa
Yoshito Fukumoto
T. Superconductivity Research Laboratory Wada
S. Superconductivity Research Laboratory Koriyama
T. Superconductivity Research Laboratory Sakurai
N. Superconductivity Research Laboratory Suzuki
H. Superconductivity Research Laboratory Yamauchi
S. Superconductivity Research Laboratory Tanaka
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Kyocera Corp
International Superconductivity Technology Center
Kobe Steel Ltd
Mitsubishi Materials Corp
Panasonic Holdings Corp
Tokyo Electric Power Company Holdings Inc
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Kyocera Corp
Tokyo Electric Power Co Inc
International Superconductivity Technology Center
Kobe Steel Ltd
Mitsubishi Materials Corp
Matsushita Electric Industrial Co Ltd
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Priority claimed from JP1176472A external-priority patent/JP2763075B2/ja
Priority claimed from JP1230754A external-priority patent/JPH04164855A/ja
Priority claimed from JP1230756A external-priority patent/JPH04167313A/ja
Priority claimed from JP1283650A external-priority patent/JPH05124815A/ja
Application filed by Kyocera Corp, Tokyo Electric Power Co Inc, International Superconductivity Technology Center, Kobe Steel Ltd, Mitsubishi Materials Corp, Matsushita Electric Industrial Co Ltd filed Critical Kyocera Corp
Publication of EP0436723A1 publication Critical patent/EP0436723A1/de
Publication of EP0436723A4 publication Critical patent/EP0436723A4/en
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    • C—CHEMISTRY; METALLURGY
    • C01—INORGANIC CHEMISTRY
    • C01G—COMPOUNDS CONTAINING METALS NOT COVERED BY SUBCLASSES C01D OR C01F
    • C01G3/00—Compounds of copper
    • C01G3/006—Compounds containing, besides copper, two or more other elements, with the exception of oxygen or hydrogen
    • C—CHEMISTRY; METALLURGY
    • C01—INORGANIC CHEMISTRY
    • C01G—COMPOUNDS CONTAINING METALS NOT COVERED BY SUBCLASSES C01D OR C01F
    • C01G3/00—Compounds of copper
    • C—CHEMISTRY; METALLURGY
    • C04—CEMENTS; CONCRETE; ARTIFICIAL STONE; CERAMICS; REFRACTORIES
    • C04B—LIME, MAGNESIA; SLAG; CEMENTS; COMPOSITIONS THEREOF, e.g. MORTARS, CONCRETE OR LIKE BUILDING MATERIALS; ARTIFICIAL STONE; CERAMICS; REFRACTORIES; TREATMENT OF NATURAL STONE
    • C04B35/00—Shaped ceramic products characterised by their composition; Ceramics compositions; Processing powders of inorganic compounds preparatory to the manufacturing of ceramic products
    • C04B35/01—Shaped ceramic products characterised by their composition; Ceramics compositions; Processing powders of inorganic compounds preparatory to the manufacturing of ceramic products based on oxide ceramics
    • C04B35/45—Shaped ceramic products characterised by their composition; Ceramics compositions; Processing powders of inorganic compounds preparatory to the manufacturing of ceramic products based on oxide ceramics based on copper oxide or solid solutions thereof with other oxides
    • C04B35/4504—Shaped ceramic products characterised by their composition; Ceramics compositions; Processing powders of inorganic compounds preparatory to the manufacturing of ceramic products based on oxide ceramics based on copper oxide or solid solutions thereof with other oxides containing rare earth oxides
    • H—ELECTRICITY
    • H10—SEMICONDUCTOR DEVICES; ELECTRIC SOLID-STATE DEVICES NOT OTHERWISE PROVIDED FOR
    • H10N—ELECTRIC SOLID-STATE DEVICES NOT OTHERWISE PROVIDED FOR
    • H10N60/00—Superconducting devices
    • H10N60/01—Manufacture or treatment
    • H10N60/0268—Manufacture or treatment of devices comprising copper oxide
    • H10N60/0801—Manufacture or treatment of filaments or composite wires
    • H—ELECTRICITY
    • H10—SEMICONDUCTOR DEVICES; ELECTRIC SOLID-STATE DEVICES NOT OTHERWISE PROVIDED FOR
    • H10N—ELECTRIC SOLID-STATE DEVICES NOT OTHERWISE PROVIDED FOR
    • H10N60/00—Superconducting devices
    • H10N60/80—Constructional details
    • H10N60/85—Superconducting active materials
    • H10N60/855—Ceramic superconductors
    • H10N60/857—Ceramic superconductors comprising copper oxide
    • C—CHEMISTRY; METALLURGY
    • C01—INORGANIC CHEMISTRY
    • C01P—INDEXING SCHEME RELATING TO STRUCTURAL AND PHYSICAL ASPECTS OF SOLID INORGANIC COMPOUNDS
    • C01P2002/00—Crystal-structural characteristics
    • C01P2002/70—Crystal-structural characteristics defined by measured X-ray, neutron or electron diffraction data
    • C01P2002/72—Crystal-structural characteristics defined by measured X-ray, neutron or electron diffraction data by d-values or two theta-values, e.g. as X-ray diagram
    • C—CHEMISTRY; METALLURGY
    • C01—INORGANIC CHEMISTRY
    • C01P—INDEXING SCHEME RELATING TO STRUCTURAL AND PHYSICAL ASPECTS OF SOLID INORGANIC COMPOUNDS
    • C01P2002/00—Crystal-structural characteristics
    • C01P2002/70—Crystal-structural characteristics defined by measured X-ray, neutron or electron diffraction data
    • C01P2002/77—Crystal-structural characteristics defined by measured X-ray, neutron or electron diffraction data by unit-cell parameters, atom positions or structure diagrams
    • C—CHEMISTRY; METALLURGY
    • C01—INORGANIC CHEMISTRY
    • C01P—INDEXING SCHEME RELATING TO STRUCTURAL AND PHYSICAL ASPECTS OF SOLID INORGANIC COMPOUNDS
    • C01P2002/00—Crystal-structural characteristics
    • C01P2002/80—Crystal-structural characteristics defined by measured data other than those specified in group C01P2002/70
    • C01P2002/88—Crystal-structural characteristics defined by measured data other than those specified in group C01P2002/70 by thermal analysis data, e.g. TGA, DTA, DSC
    • C—CHEMISTRY; METALLURGY
    • C01—INORGANIC CHEMISTRY
    • C01P—INDEXING SCHEME RELATING TO STRUCTURAL AND PHYSICAL ASPECTS OF SOLID INORGANIC COMPOUNDS
    • C01P2004/00—Particle morphology
    • C01P2004/80—Particles consisting of a mixture of two or more inorganic phases
    • C—CHEMISTRY; METALLURGY
    • C01—INORGANIC CHEMISTRY
    • C01P—INDEXING SCHEME RELATING TO STRUCTURAL AND PHYSICAL ASPECTS OF SOLID INORGANIC COMPOUNDS
    • C01P2006/00—Physical properties of inorganic compounds
    • C01P2006/14—Pore volume

Definitions

  • the present invention concerns an oxide superconductor having a superconducting transition temperature (hereinafter sometimes referred to simply as Tc) sufficiently higher than the liquid nitrogen temperature and less suffering from a problem of releasing oxygen during fabrication to result in fluctuating of Tc, as well as a method of manufacturing such an oxide superconductor.
  • Tc superconducting transition temperature
  • the oxide super conductor described above has a nature that oxygen atoms as a constituent element is liable to be released by the effect of heat during fabrication and, accordingly, the oxygen content varies depending on the conditions for heat treatment upon fabrication, which is accompanied by orthorhombic tetragonal phase transformation and this greatly varies Tc within a range from 0K to 90K (Phys. Rev. B36 (1987) p5719).
  • RBa2Cu4O8 type oxides have been noted as an important substance from a practical point of view since they are stable with no release of oxygen even under heating up to about 850° C and they have Tc of about 80K, which is higher than the liquid nitrogen temperature.
  • RBa2Cu4O8 type oxides have Tc higher than the liquid nitrogen temperature, it is about 80K in each of them and the liquid nitrogen temperature margin is too small, it is difficult for practical application and, accordingly, it has been expected for the development of an RBa2Cu4O8 type oxide having higher Tc.
  • the present invention has been achieved in order to overcome such technical problems and an object thereof is to provide a stable oxide superconductor having Tc sufficiently higher than the liquid nitrogen temperature and not causing release of oxygen at high temperature during fabrication, as well as a method of manufacturing such an oxide superconductor.
  • An oxide superconductor according to the present invention is an oxide superconductor represented by the chemical formula :(R 1-x Ca x )Ba2Cu4O8, wherein R is one or more of elements selected from the group consisting of Y and lanthanide series rare earth elements, and x is within a range: 0.001 ⁇ x ⁇ 0.5.
  • R is one or more of elements selected from the group consisting of Y and lanthanide series rare earth elements, and x is within a range: 0.001 ⁇ x ⁇ 0.5.
  • One of the most prominent features of the oxide superconductor according to the present invention is that a portion of R in RBa2Cu4O8 is partially substituted with Ca, by which Tc is as high as about 90K and excellent stability is also provided against high temperature heat treatment.
  • a stable superconducting wire material can be prepared without deteriorating superconducting characteristics even after the sintering heat treatment as a final step.
  • the above-mentioned oxide superconductor can be formed by various methods such as sputtering and, in particular, a method of applying a hot isostatic pressing treatment to a starting powder mixture for manufacturing an oxide superconductor comprising R (R having the same meanings as described above), Ca, Ba, Cu and O in a mixed atmosphere of an inert gas and an oxygen gas, within a temperature range of 850 to 1100° C is effective.
  • an oxide superconductor can be manufactured at a higher efficiency by hindering the formation of an oxide as an intermediate material represented by (R 1-x Ca x )Ba2Cu3O7 (in which x represents the same range as described above and also hereinafter) during manufacturing step, that is, before hot isostatic pressing treatment.
  • the present inventors have made a study from various aspects in order to realize a stable superconductor having Tc sufficiently higher than the liquid nitrogen temperature and not causing the release of oxygen even at a high temperature.
  • the present inventors have at first made various studies on the optimum form in view of the structure of a RBa2Cu4O8 type oxide. As a result, it has been found in a RBa2Cu4O8 type oxide in which single CuO chains are changed into double CuO chains in a three-layered perovskite RBa2Cu3O7 type crystal structure that (R 1-x Ca x )Ba2Cu4O8 type oxide in which from 0.1 to 50 atm% of R is substituted with Ca has Tc sufficiently higher than the liquid nitrogen temperature by the effect of Ca substitution and can be fabricated stably with no release of oxygen even under a heating condition near 850° C.
  • Fig. 1 shows a structure of RBa2Cu4O8 as a fundamental structure of the oxide superconductor according to the present invention and Fig. 2 shows a structure of a conventional RBa2Cu3O7.
  • 1 represents R
  • 2 represents Ba
  • 3 represents Cu
  • 4 represents O arranged at the intersections of linear segments respectively.
  • the oxide superconductor (R 1-x Ca x )Ba2Cu4O8 according to the present invention is a RBa2Cu4O8 oxide having double CuO chains instead of single CuO chains in the perovskite RBa2Cu3O7 type of a three layered crystal structure shown in Fig. 1, wherein from 0.1 to 50 atm% of R is substituted with Ca. Remarkable elevation of Tc by the Ca substitution is the most prominent feature of the present invention.
  • an aimed superconductor wire material can be obtained by packing the powder into a sheath material, drawing the material and then applying sintering.
  • the amount of the Ca substitution for the (R 1-x Ca x )Ba2Cu4O8 type oxide is defined as from 0.001 to 0.5 with the reasons described below. That is, the effect of the substitution appears with x of greater than 0.001, whereas x does not substantially exceed 0.5 under the conditions for the manufacturing method according to the present invention.
  • a preferred range is from 0.001 to 0.2.
  • it is preferred to define the composition of the starting material powder as: R or (R + Ca):Ba:Cu 1:2:4 in order to form the phase stably.
  • oxides such as Y2O3, R2O3, CaO, BaO and Cu2O may be used preferably with a view to easily proceeding the forming reaction.
  • the (R 1-x Ca x )Ba2Cu4O8 according to the Present invention can be manufactured by various kinds of methods such as sputtering and coprecipitation.
  • the (R 1-x Ca x )Ba2O4O8 according to the present invention can be manufactured by using various kinds of methods such as sputtering or coprecipitation as has been described above, but it has been found that the method of using HIP as a means for manufacturing the (R 1-x Ca x )Ba x Cu4O8 is effective. That is it has been found that an aimed (R 1-x Ca x )Ba2Cu4O8 type oxide superconductor can be obtained at a high efficiency by applying a HIP treatment within a temperature range of 850 to 1100° C in a mixed atmosphere of an inert gas and an oxygen gas. This is referred to as an O2-HIP method.
  • the HIP treatment in O2-HIP method in the present invention is a treatment in a mixed atmosphere of an inert gas and an oxygen gas. Accordingly, if the same pressure as that with pure oxygen (for example 20MPa (200 atm)) is to be attained by an oxygen partial pressure, the total pressure as the mixed atmosphere can be increased remarkably. For instance, it is considered that if the molar ratio of the inert gas and oxygen is defined as 1:1, the total pressure can be made to 40MPa (400 atm), while the total pressure may be increased to 100MPa (1000 atm) if the ratio is defined as 4:1 by which the diffusion of Cu atoms is further improved to promote the formation of (R 1-x Ca x )Ba2Cu4O8 type oxide super conductor. Further, this can provide a great merit also in view of the operation safety, as compared with the case of increasing the total pressure by pure oxygen.
  • the temperature for the HIP treatment in the manufacture of the (R 1-x Ca x )Ba2Cu4O8 type oxide superconductor is at least higher than 850° C with a view point of suppressing the formation of the RBa2Cu3O7 type oxide and promoting the formation of the (R 1-x Ca x )Ba2Cu4O8 type oxide.
  • starting material powders may be mixed previously, then fabricated into a thin film or wire and, subsequently, applied with a HIP treatment into a superconductor, or (2) a HIP treatment may be applied in a powdery state of the starting material into a superconductor and then fabricating the material into a thin film or wire.
  • the 1-2-4 phase is more decomposable as compared with the 1-2-3 phase, if the HIP treatment at a high temperature is continued for a long period of time, there is a disadvantage that the 1-2-4 phase once formed is again decomposed into the 1-2-3 phase.
  • the present inventors have made a study with a view point of manufacturing the (R 1-x Ca x )Ba2O4O8 type oxide superconductor in a short period of time and at a high yield.
  • the intended purpose can be attained more effectively, by avoiding a heat treatment step easily forming the 1-2-3 phase as much as possible, applying the HIP treatment to the starting material powder in a state where the 1-2-3 phase is not formed thereby directly forming the 1-2-4 phase, and terminating the reaction in a state of suppressing the once formed 1-2-4 phase from being decomposed into the 1-2-3 phase.
  • the oxide superconductor provided by the present invention has a characteristic constitution of having a chemical structure of the 1-2-4 phase as apparent from the description throughout the specification but it will be understood easily by those skilled in the art that this does not mean to positively exclude the incorporation of the 1-2-3 phase to some extent providing that this does not hinder the advantageous effect of the present invention.
  • Figs. 3 and 4 are powder X-ray diffraction patterns for YBa2Cu4O8 and Fig. 4 for a powder X-ray diffraction pattern for Y 0.9 Ca 0.1 Ba2Cu4O8.
  • numerals in the figures represent indices for the peaks in the X-ray diffractiometry.
  • Specimens for the resistance measurement were prepared by molding the superconducting powders of (Y 1-x Ca x )Ba2Cu4O8 described above in a rectangular powder molding die and then applying a sintering treatment in air at 800° C for 24 hrs.
  • the results for the measurement of the superconducting characteristics are shown in Fig. 5 (temperature vs resistivity characteristics diagram) and in Table 1.
  • Tc on is a temperature at which superconducting transition begins from the ordinary conducting state
  • each of the specimens for the superconducting powder of (Y 1-x Ca x )Ba2Cu4O8 according to the present invention has Tc of about 90K, and 90K is a sufficiently higher temperature than 77K of the liquid nitrogen temperature.
  • Fig. 6 is a graph illustrating the result of the thermogravimetric analysis for (Y 1-x Ca x )Ba2Cu4O8 obtained in Example 1. It can be seen that the weight does not change and is stable up to 850° C.
  • the product was heated at 200° C/hr, maintained at 960° C for 6 hrs, further heated upto 1050° C at a rate of 200° C/hr and then maintained at that temperature for 6 hours. Cooling was conducted down to 300° C at a rate of 200° C/hr, and the specimen was taken out into air after reducing the pressure to 0.1MPa (1 atm.). The specimen was pulverized again and molded. The molding product was sintered in oxygen at 800° C or 20 hours to obtain a predetermined specimen.
  • the resultant phase of the thus obtained sintering product of (Y 1-x Ca x )Ba2Cu4O8 was confirmed by using powdery X-ray diffractiometry. It has been confirmed that any of the main ingredients in the resultant specimen had a YBa2Cu4O8 crystal structure.
  • the second phase is slightly observed in this specimen.
  • the resultant phases of the specimens were collectively shown in Table 2. It has a (Y 1-x Ca x )Ba2Cu4O8 single phase within a range of x from 0 to 0.2 and contains the second phase when x reaches 0.25.
  • each of the superconducting specimens of (Y 1-x Ca x )Ba2Cu4O8 in this example shows a superconducting transition temperature in the order of 90K.
  • the superconducting transition temperature is a temperature sufficiently higher than the boiling point of liquid nitrogen (77K).
  • the resistance value at room temperature is lowered along with the increase for the content x of Ca. In this way, a high critical current density can be expected for a specimen with low resistance value at a room temperature.
  • the superconductor YBa2Cu4O8 as the matrix has a superconducting transition temperature at 80K and is less sinterable and the sintering product has a porosity of greater than 30%, wherein it has a composition of (Y 1-x Ca x )Ba2Cu4O8 and each of the specimens in the example has a superconducting transition temperature at 90K and the sintering product has a porosity of less than 10%. Furthermore, it could be confirmed that these specimens had low electric resistivity at a room temperature, and they were present stably with neither intrusion nor release of oxygen up to about 850° C according to thermal analysis.
  • Example 0.6 Superconducting phase+impurity phase 94 72 7.2 6
  • each of the superconductor specimens (Ho 1-x Ca x )Ba2Cu4O8 in this example shows a superconducting transition temperature at an order of 90K.
  • the superconducting transition temperature is sufficiently higher than the boiling point of the liquid nitrogen, (77K).
  • the resistance value at the room temperature is lowered along with the increase of the Ca content x.
  • a high critical current density can be expected for such specimens with low resistance value at the room temperature.
  • the superconductor HoBa2Cu4O8 as the matrix has a Tc of 80K and is less sinterable and, accordingly, the porosity of the sintering product is more than 30%
  • a specimen having the composition of (Ho 1-x Ca x )Ba2Cu4O8 and x within a range of 0.001 ⁇ X ⁇ 0.5 has a superconducting transition temperature at about 90K and the porosity of the sintering product is less than 20%.
  • the specimens have low electric resistivity at a room temperature and is present stably with neither intrusion nor release of oxygen upto about 850° C by thermal analysis.
  • the oxide superconductor according to the present invention is stable without deteriorating superconducting characteristics in the sintering heat treatment step as the final step in the case of fabricating into a sheath wire, as well as it is easily sinterable, a superconducting wire of high critical current density in which each of particles is sintered at high density can be manufactured.
  • the oxide superconductor according to the present invention can be molded at a high density in a case of applying high temperature molding by using a binder. That is, the conventional superconductor RBa2Cu3O7 can not be removed with the binder at a temperature higher than 400° C, the binder can be removed at lower than 800° C in the case of the superconductor according to the present invention. Since this enables high density molding, the superconducting current density can be improved further.
  • Figs. 13 and 14 corresponds to Y 0.9 Ca 0.1 Ba2Cu4O8 (980° C, HIP) and Fig. 14 corresponds to Ho 0.95 Ca 0.05 Ba2Cu4O7 (930° C, HIP).
  • the powder X-ray pattern in Fig. 13 shows that the resultant powder phase shows the YBa2Cu4O8 type structure, while the powder X-ray pattern in Fig. 14 shows that the resultant powder phase shows the YBa2Cu4O8 type structure and that it slightly contains a YBa2Cu3O7 type structure.
  • Figs. 15 and 16 corresponds to Y 0.9 Ca 0.1 Ba2Cu4O8 (980° C, HIP), while Fig. 16 corresponds to Ho 0.95 Ca 0.05 Ba2Cu4O8 (930° C, HIP).
  • the (R 1-x Ca x )Ba2 Cu4O8 type oxide obtained according to the present invention shows high value also for Tc.
  • the resultant powders were subjected to X-ray diffractiometry to determine the phases contained, and the Meissner volume fraction at 4.2K and the Tc value were measured for the sample only consisting of the 1-2-4 phase.
  • Figs. 17 and 18 corresponds to Ho 0.95 Ca 0.05 Ba2Cu4O8.
  • the powder X-ray pattern in Fig. 17 shows that the resultant powder phase shows the YBa2Cu4O8 type structure, while the powder X-ray pattern in Fig. 18 shows that the resultant powder phase shows the YBa2Cu4O8 type structure.
  • Fig. 19 corresponds to (Y 0.9 Ca 0.1 )Ba2Cu4O8.
  • the resultant superconducting powder was packed in a silver tube of 5 mm outer diameter, 3 mm inner diameter and 80 mm length one end of the tube was tightly sealed with a silver cap and, subsequently, the pipe was tightly sealed at one end thereof with a silver cap and closed at the other end thereof with a silver cap having a small aperture (0.1 mm ⁇ ), evacuated to 1330Pa (101 Torr) so as not to scatter the powder and, finally, the tube was sealed by crushing the cap. After drawing it into a wire of 0.75 mm ⁇ in outer diameter by swaging fabrication, it was applied with roll fabrication into a tape-shape of 0.2 mm thickness.
  • Jc in Table 8 is a critical current density under liquid nitrogen temperature (77K).
  • oxide superconductor having a superconducting transition temperature sufficiently higher than the liquid nitrogen temperature and causing no release of oxygen at a high temperature during fabrication, as well as a method capable of obtaining such an oxide superconductor in a short period of time and at a high yield.
  • the oxide superconductor according to the present invention can be used generally in the field such as wirings and magnetic shieldings for low temperature electronic apparatus.

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Claims (9)

  1. Oxid-Supraleiter, dargestellt durch die chemische Formel (R1-xCax)Ba₂Cu₄O₈, wobei R ein oder mehrere Elemente umfaßt, die aus der Gruppe ausgewählt sind, die aus Y und Seltenerdelementen der Lanthanreihe besteht, und x in einem Bereich 0,001 ≦ x ≦ 0,5 ist.
  2. Oxid-Supraleiter nach Anspruch 1, wobei R Y ist und x in einem Bereich 0,001 ≦ x ≦ 0,2 ist.
  3. Oxid-Supraleiter nach Anspruch 1, wobei R Y ist und x in einem Bereich 0,2 ≦ x ≦ 0,5 ist.
  4. Verfahren zur Herstellung eines Oxid-Supraleiters mit der Struktur (R1-xCax)Ba₂Cu₄O₈, wobei R und x wie in Anspruch 1 definiert sind, das das Calcinieren von Ausgangsmaterialpulvern und dann die Anwendung einer heißen isostatischen Druckbehandlung in einer vermischten Atmosphäre aus einem inerten Gas und einem Sauerstoffgas umfaßt.
  5. Verfahren zur Herstellung eines Oxid-Supraleiters, bei dem ein Oxid-Supraleiter, der ein durch



            (R1-xCax)Ba₂Cu₄O₈



    (wobei x von 0,001 bis 0,5 ist und R dieselbe Bedeutung wie vorstehend beschrieben hat) dargestelltes Oxid enthält, durch Anwenden einer heißen isostatischen Druckbehandlung auf eine Ausgangspulvermischung zur Herstellung eines OxidSupraleiters mit R (worin R ein oder mehrere Elemente umfaßt, die aus der Gruppe ausgewählt sind, die aus Y und Seltenerdelementen der Lanthanreihe besteht), Ca, Ba, Cu und O in einer vermischten Atmosphäre aus einem inerten Gas und Sauerstoff in einem Temperaturbereich von 850 bis 1100 °C gebildet wird.
  6. Herstellungsverfahren nach Anspruch 5, wobei R Y ist und x in einem Bereich 0,001 ≦ x ≦ 0,2 liegt.
  7. Herstellungsverfahren nach einem der Ansprüche 5 oder 6, wobei ein Oxid-Supraleiter, der ein durch (R1-xCax)Ba₂Cu₄O₈ dargestelltes Oxid enthält, gebildet wird, ohne ein Oxid, das durch (R1-xCax)Ba₂Cu₃O₇ dargestellt wird, als Zwischenprodukt vor der heißen isostatischen Druckbehandlung zu bilden.
  8. Verfahren zur Herstellung eines Oxid-Supraleiterdrahts, das die Bildung eines Oxid-Supraleiterpulvers, das ein durch



            (R1-xCax)Ba₂Cu₄O₈



    (worin x von 0,001 bis 0,5 ist und R dieselbe Bedeutung wie vorstehend beschrieben hat) dargestelltes Oxid enthält, durch Anwenden einer heißen isostatischen Druckbehandlung auf eine Ausgangspulvermischung zur Herstellung eines Oxid-Supraleiters mit R (wobei R ein oder mehrere Elemente umfaßt, die aus der Gruppe ausgewählt sind, die aus Y und Seltenerdelementen der Lanthanreihe besteht), Ca, Ba, Cu und O in einer vermischten Atmosphäre aus einem inerten Gas und einem Sauerstoffgas in einem Temperaturbereich von 850 bis 1100°C, Füllen des Pulvers in ein Umhüllungselement, Ziehen desselben zu einem Draht und dann Anwenden von Sintern umfaßt.
  9. Herstellungsverfahren nach Anspruch 8, bei dem ein Oxid-Supraleiterpulver, das ein durch (R1-xCax)Ba₂Cu₄O₈ dargestelltes Oxid enthält, gebildet wird, ohne ein Oxid, das durch (R1-xCax)Ba₂Cu₃O₇ dargestellt wird, als Zwischenprodukt vor der heißen isostatischen Druckbehandlung zu bilden.
EP90910173A 1989-07-07 1990-07-07 Oxyde supraleitfahiges mittel und verfahren zur herstellung Expired - Lifetime EP0436723B1 (de)

Applications Claiming Priority (15)

Application Number Priority Date Filing Date Title
JP1176472A JP2763075B2 (ja) 1989-07-07 1989-07-07 酸化物超電導体
JP176472/89 1989-07-07
JP213723/89 1989-08-18
JP21372389 1989-08-18
JP213722/89 1989-08-18
JP21373089 1989-08-18
JP213730/89 1989-08-18
JP21372289 1989-08-18
JP230754/89 1989-09-06
JP1230754A JPH04164855A (ja) 1989-09-06 1989-09-06 酸化物超電導体の製造方法
JP1230756A JPH04167313A (ja) 1989-09-06 1989-09-06 酸化物超電導体線材の製造方法
JP230756/89 1989-09-06
JP283650/89 1989-10-30
JP1283650A JPH05124815A (ja) 1989-10-30 1989-10-30 酸化物超電導体の製造方法
PCT/JP1990/000877 WO1991000847A1 (en) 1989-07-07 1990-07-07 Oxide superconductor and method of producing the same

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EP0436723A1 EP0436723A1 (de) 1991-07-17
EP0436723A4 EP0436723A4 (en) 1992-01-08
EP0436723B1 true EP0436723B1 (de) 1995-06-21

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EP90910173A Expired - Lifetime EP0436723B1 (de) 1989-07-07 1990-07-07 Oxyde supraleitfahiges mittel und verfahren zur herstellung

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EP (1) EP0436723B1 (de)
KR (1) KR0159487B1 (de)
DE (1) DE69020327T2 (de)
WO (1) WO1991000847A1 (de)

Family Cites Families (5)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JPS649850A (en) * 1987-06-30 1989-01-13 Agency Ind Science Techn Superconducting material and production thereof
US4857504A (en) * 1987-08-25 1989-08-15 University Of Arkansas Melt-produced high temperature rare earth barium copper oxide superconductor and processes for making same
JPH01111766A (ja) * 1987-10-26 1989-04-28 Toshiba Corp 高温超伝導セラミックス
JP2596964B2 (ja) * 1988-04-04 1997-04-02 三菱化学株式会社 酸化物超伝導材料
JPH0218321A (ja) * 1988-07-04 1990-01-22 Japan Atom Energy Res Inst Ｌａ−Ｂａ−Ｃａ−Ｃｕ酸化物超伝導体

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KR920701047A (ko) 1992-08-11
DE69020327D1 (de) 1995-07-27
KR0159487B1 (ko) 1998-11-16
WO1991000847A1 (en) 1991-01-24
DE69020327T2 (de) 1995-11-16
EP0436723A4 (en) 1992-01-08
EP0436723A1 (de) 1991-07-17

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